JP3375868B2 - Low hydrogen coated arc welding rod for high Cr ferritic heat resistant steel - Google Patents
Low hydrogen coated arc welding rod for high Cr ferritic heat resistant steelInfo
- Publication number
- JP3375868B2 JP3375868B2 JP33620097A JP33620097A JP3375868B2 JP 3375868 B2 JP3375868 B2 JP 3375868B2 JP 33620097 A JP33620097 A JP 33620097A JP 33620097 A JP33620097 A JP 33620097A JP 3375868 B2 JP3375868 B2 JP 3375868B2
- Authority
- JP
- Japan
- Prior art keywords
- weight
- toughness
- arc welding
- welding rod
- coated arc
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
Landscapes
- Arc Welding In General (AREA)
- Nonmetallic Welding Materials (AREA)
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、主に９乃至１２重
量％のＣｒを含有する低合金鋼を溶接対象として高温に
おけるクリープ強度と靭性が優れた溶接金属を得ること
ができる高Ｃｒフェライト系耐熱鋼用低水素系被覆アー
ク溶接棒に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention mainly relates to a low alloy steel containing 9 to 12% by weight of Cr and is capable of obtaining a weld metal excellent in creep strength and toughness at high temperature and having a high Cr ferrite content. The present invention relates to a low-hydrogen coated arc welding rod for heat-resistant steel.
【０００２】[0002]
【従来の技術】従来より、火力発電用ボイラの主蒸気管
又は過熱器管等の素材として、フェライト系耐熱鋼であ
るＣｒ−Ｍｏ鋼が使用されており、溶接材料も同鋼種用
のものが適用されてきた。しかし、近時、これらの主蒸
気管又は過熱器管等の材料としては、高温における高強
度化が要求されている。これは、省エネルギーの観点か
ら発電効率の向上を狙いとしており、高温稼働によりＣ
Ｏ2排出量の削減を考慮したものである。なお、高い高
温強度を有する材料としてオーステナイト系ステンレス
鋼があるが、このオーステナイト系ステンレス鋼は、熱
膨張率、熱伝導度及び耐応力腐食割れ性等が劣っている
ため、この種の用途には適用できない。このため、この
種の用途には、高Ｃｒフェライト系耐熱鋼を採用せざる
を得ず、高Ｃｒフェライト系耐熱鋼用溶接材料の高温高
強度化に対する要求が強い。2. Description of the Related Art Conventionally, Cr-Mo steel, which is a ferritic heat-resistant steel, has been used as a material for a main steam pipe or a superheater pipe of a boiler for thermal power generation, and a welding material for the same grade is also used. Has been applied. However, recently, as materials for these main steam pipes, superheater pipes, and the like, high strength at high temperatures is required. This aims to improve power generation efficiency from the viewpoint of energy saving, and C
This is because the reduction of O 2 emission is taken into consideration. Note that there is austenitic stainless steel as a material having high high-temperature strength, but this austenitic stainless steel is inferior in thermal expansion coefficient, thermal conductivity, stress corrosion cracking resistance, etc. Not applicable. For this reason, high Cr ferritic heat-resisting steel must be used for this type of application, and there is a strong demand for high-temperature, high-strength welding materials for high Cr ferritic heat-resisting steel.
【０００３】この高Ｃｒフェライト系耐熱鋼において、
高温高強度を達成するためには９乃至１２重量％のＣｒ
を含有する必要がある。このＣｒ量により、高温高強度
（クリープ強度）、及び耐食性が優れた溶接金属を得る
ことができる。このクリープ強度等が高くなると、一般
的に、靭性は低下する傾向にある。このため、これらの
鋼種において、クリープ強度と靭性を両立させるため
に、これまでに多くの溶接材料が提案されている。例え
ば、９重量％Ｃｒ低合金鋼用被覆アーク溶接棒として特
開平５−１６１９９３号などが開示されている。この被
覆アーク溶接棒は、心線及び／又は被覆剤中の成分
（Ｃ、Ｍｎ、Ｓｉ、Ｃｒ、Ｍｏ、Ｎｉ、Ｎ、Ｖ、Ｎｂ）
を規制して、クリープ強度と靭性の向上を図ったもので
ある。また、９乃至１２重量％Ｃｒ鋼用被覆アーク溶接
棒として特開平７−２６８５６２号が開示されている。
この被覆アーク溶接棒は、被覆アーク溶接棒全重量に対
して、成分（Ｃ、Ｓｉ、Ｍｎ、Ｃｒ、Ｍｏ、Ｖ、Ｎｂ、
Ｗ、Ｎ、Ｃｏ、Ｎｉ）を規制して、クリープ強度、靭
性、及び耐割れ性の向上を図ったものである。In this high Cr ferritic heat resistant steel,
9 to 12 wt% Cr to achieve high temperature and high strength
Must be included. This amount of Cr makes it possible to obtain a weld metal having excellent high temperature high strength (creep strength) and corrosion resistance. When the creep strength and the like increase, the toughness generally tends to decrease. Therefore, in these steel types, many welding materials have been proposed so far in order to achieve both creep strength and toughness. For example, JP-A-5-161993 is disclosed as a coated arc welding rod for 9 wt% Cr low alloy steel. This coated arc welding rod has a core wire and / or components (C, Mn, Si, Cr, Mo, Ni, N, V, Nb) in the coating agent.
Are regulated to improve creep strength and toughness. Further, JP-A-7-268562 is disclosed as a coated arc welding rod for 9 to 12 wt% Cr steel.
This coated arc welding rod contains the components (C, Si, Mn, Cr, Mo, V, Nb,
(W, N, Co, Ni) is regulated to improve creep strength, toughness, and crack resistance.
【０００４】[0004]
【発明が解決しようとする課題】しかし、これらの従来
の被覆アーク溶接棒では、近時の９乃至１２重量％Ｃｒ
耐熱鋼用溶接材料として求められる高い靭性と高クリー
プ強度の性能を、十分満足しているとはいえない。靭性
及びクリープ強度はいずれもＳＲ（溶接後応力除去焼な
まし）条件に大きく依存し、またクリープ強度は使用温
度と負荷応力に大きく影響を受ける。このため、実用化
に当たっては安全性を考慮して、より高性能の溶接金属
が求められている。However, in these conventional coated arc welding rods, the recent 9 to 12 wt% Cr
It cannot be said that the high toughness and high creep strength properties required for a welding material for heat-resistant steel are sufficiently satisfied. Both toughness and creep strength largely depend on SR (post-welding stress relief annealing) conditions, and creep strength is greatly affected by operating temperature and load stress. For this reason, in practical use, in consideration of safety, higher performance weld metal is required.
【０００５】本発明はかかる問題点に鑑みてなされたも
のであって、フェライト系耐熱鋼用被覆アーク溶接棒、
特に９乃至１２重量％のＣｒを含有する低合金鋼を溶接
する場合に、高温におけるクリープ強度と靭性が優れた
溶接金属が得られる高Ｃｒフェライト系耐熱鋼用低水素
系被覆アーク溶接材を提供することを目的とする。The present invention has been made in view of the above problems, and a covered arc welding rod for ferritic heat resistant steel,
Provided is a low hydrogen coated arc welding material for high Cr ferritic heat resistant steel, which can obtain a weld metal having excellent creep strength and toughness at high temperature especially when welding a low alloy steel containing 9 to 12% by weight of Cr. The purpose is to do.
【０００６】[0006]
【課題を解決するための手段】本発明に係る高Ｃｒフェ
ライト系耐熱鋼用低水素系被覆アーク溶接材は、心線及
び被覆剤の一方又は双方の中に、被覆アーク溶接棒全重
量当たり、Ｃ：０．０４乃至０．１０重量％、Ｓｉ：
０．５乃至２．０重量％、Ｍｎ：０．５乃至１．５重量
％、Ｎｉ：０．４乃至１．５重量％、Ｃｒ：６．０乃至
１２．０重量％、Ｍｏ：０．０５乃至０．２５重量％、
Ｔｉ：０．０１乃至０．０５重量％、Ｖ：０．１０乃至
０．４０重量％、Ｎｂ：０．０２乃至０．１０重量％、
Ｗ：０．７乃至２．０重量％、Ｃｏ：２．０重量％以
下、Ｎ：０．０２乃至０．１０重量％を含有したことを
特徴とする。A low hydrogen system coated arc welding material for a high Cr ferritic heat resistant steel according to the present invention comprises, in one or both of a core wire and a coating material, a total weight of a coated arc welding rod, C: 0.04 to 0.10% by weight, Si:
0.5 to 2.0% by weight, Mn: 0.5 to 1.5% by weight, Ni: 0.4 to 1.5% by weight, Cr: 6.0 to 12.0% by weight, Mo: 0. 05 to 0.25% by weight,
Ti: 0.01 to 0.05% by weight, V: 0.10 to 0.40% by weight, Nb: 0.02 to 0.10% by weight,
W: 0.7 to 2.0 wt%, Co: 2.0 wt% or less, N: 0.02 to 0.10 wt% are contained.
【０００７】[0007]
【発明の実施の形態】本発明者等は本発明の課題を解決
すべく、即ち、クリープ強度及び靭性が優れた溶接金属
を得ると共に、良好な溶接作業性を得ることができる低
水素系被覆アーク溶接棒を開発すべく、心線及び被覆剤
の成分と、溶接金属の機械的性質並びに析出物及び組織
等との関係を究明するために、種々の実験研究を行っ
た。その結果、以下の事実が判明した。BEST MODE FOR CARRYING OUT THE INVENTION In order to solve the problems of the present invention, the present inventors obtain a weld metal having excellent creep strength and toughness, and a low hydrogen type coating capable of obtaining good welding workability. In order to develop an arc welding rod, various experimental studies were carried out in order to investigate the relationship between the components of the core wire and the coating material, the mechanical properties of the weld metal, the precipitates and the microstructure. As a result, the following facts were revealed.
【０００８】（１）クリープ強度は、ＭＸ（炭窒化物）
の析出物の量の増加に伴い、向上する。(1) Creep strength is MX (carbonitride)
It increases with the increase of the amount of precipitates.
【０００９】（２）靭性はδフェライトの析出量とＡｅ
１変態点に大きく依存する。(2) Toughness is the amount of precipitation of δ ferrite and Ae.
1 Depends largely on the transformation point.
【００１０】（１）については、析出物の成分を構成す
るＣ、Ｃｒ、Ｔｉ、Ｖ、Ｎｂ、Ｎの含有量の影響を検討
した。そして、その中でもＴｉが靭性を比較的損なわず
に、ＴｉＮを形成して析出核となり、ＭＸの安定化及び
微細化に大きく寄与することを見出した。図１は、横軸
に被覆アーク溶接棒全重量当たりのＴｉ量（重量％）を
とり、縦軸にクリープ破断時間（時）及び吸収エネルギ
ｖＥ（０℃）（Ｊ）をとって、溶接材料の靭性に及ぼす
Ｔｉ含有量の靭性に及ぼす影響を示すグラフ図である。
この図１に示すように、Ｔｉ含有量が０．０１重量％未
満であると、クリープ破断時間が短くなる。一方、Ｔｉ
含有量が０．０５重量％を超えると、吸収エネルギが著
しく低下する。このため、靭性を高く維持しつつ高温強
度を高めるために、Ｔｉ含有量を０．０１乃至０．０５
重量％とする必要がある。Regarding (1), the influence of the contents of C, Cr, Ti, V, Nb and N constituting the components of the precipitate was examined. And, among them, it was found that Ti does not impair the toughness relatively and forms TiN to become precipitation nuclei, which greatly contributes to the stabilization and miniaturization of MX. In FIG. 1, the horizontal axis represents the Ti amount (% by weight) based on the total weight of the coated arc welding rod, and the vertical axis represents the creep rupture time (hour) and absorbed energy vE (0 ° C.) (J). FIG. 3 is a graph showing the effect of the Ti content on the toughness of Ti.
As shown in FIG. 1, when the Ti content is less than 0.01% by weight, the creep rupture time becomes short. On the other hand, Ti
If the content exceeds 0.05% by weight, the absorbed energy remarkably decreases. Therefore, in order to increase the high temperature strength while maintaining high toughness, the Ti content is set to 0.01 to 0.05.
It is necessary to set it to the weight percent.
【００１１】また、（２）については、ＳＲ時に回復を
促進させるＭｎ及びＮｉを活用する。但し、両元素はオ
ーステナイト生成作用によるδフェライトを抑制する効
果を有するが、Ａｅ１点を低下させるため、ある一定量
を超えるとＳＲ時にＳＲ温度がＡｅ１点を超えで逆変態
を起こし、靭性劣化を引き起こす。このため、Ａｅ１点
がＳＲ温度の直上になるように、各成分の含有量を規定
した。Regarding (2), Mn and Ni that promote recovery during SR are utilized. However, both elements have the effect of suppressing δ ferrite due to the austenite forming action, but since they lower the Ae1 point, if a certain amount is exceeded, the SR temperature will exceed Ae1 point during SR and reverse transformation will occur, resulting in deterioration of toughness. cause. Therefore, the content of each component is specified so that the point Ae is directly above the SR temperature.
【００１２】以下、各元素の添加理由及び組成限定理由
について詳細に説明する。これらの元素は、心線及び被
覆剤のいずれに添加しても良い。The reason for adding each element and the reason for limiting the composition will be described in detail below. These elements may be added to either the core wire or the coating material.
【００１３】Ｃ：０．０４乃至０．１０重量％
Ｃはオーステナイト安定化元素の１つであり、溶接金属
の強度を向上させる効果を有し、また低靭性の原因とな
るδフェライトの抑制作用を有する。このため、Ｃ含有
量が０．０４重量％未満ではこれらの効果を確保でき
ず、０．１０重量％を超えると耐力の上昇による靭性及
び耐割れ性の劣化を引き起こす。なお、Ｃは被覆剤から
添加する場合は、他の金属原料（Ｆｅ−Ｍｎ、金属Ｃｒ
等）に含有させて添加することができる。 C: 0.04 to 0.10 wt% C is one of the austenite stabilizing elements, has the effect of improving the strength of the weld metal, and also has the effect of suppressing δ ferrite, which causes low toughness. Have. Therefore, if the C content is less than 0.04% by weight, these effects cannot be secured, and if it exceeds 0.10% by weight, toughness and cracking resistance are deteriorated due to an increase in yield strength. When C is added from the coating agent, other metal raw materials (Fe-Mn, metal Cr) are used.
Etc.) and added.
【００１４】Ｓｉ：０．５乃至２．０重量％
ＳｉはＭｇ及びＴｉと共に脱酸剤として添加する。ま
た、Ｓｉは、クレータの形成に大きく影響を与え、立向
上進溶接には不可欠の成分であり、また強度を上昇させ
る作用がある。Ｓｉが０．５重量％未満ではその効果が
発揮されず、２．０重量％を超えると過剰な強度上昇を
生じ靭性を著しく劣化させる。なお、Ｓｉは被覆剤から
添加する場合、Ｆｅ−Ｓｉ等により添加することができ
る。 Si: 0.5 to 2.0 wt% Si is added as a deoxidizer together with Mg and Ti. Further, Si has a great influence on the formation of craters, is an indispensable component for vertical advance welding, and has an action of increasing strength. If Si is less than 0.5% by weight, the effect is not exhibited, and if it exceeds 2.0% by weight, the strength is excessively increased and the toughness is significantly deteriorated. When Si is added from the coating agent, it can be added by Fe-Si or the like.
【００１５】Ｍｎ：０．５乃至１．５重量％
Ｍｎは溶接金属の強度を向上させる作用を有するが、同
時にＳＲ時の回復促進作用により、靭性を著しく改善さ
せる効果を有する。Ｍｎが０．５重量％未満ではこれら
の効果が発揮されず、１．５重量％を超えるとクリープ
強度の劣化を引き起こす。なお、Ｍｎは被覆剤から添加
する場合、Ｆｅ−Ｍｎ、金属Ｍｎ等により添加すること
ができる。 Mn: 0.5 to 1.5 wt% Mn has the effect of improving the strength of the weld metal, but at the same time has the effect of remarkably improving the toughness due to the recovery acceleration effect during SR. If Mn is less than 0.5% by weight, these effects are not exhibited, and if it exceeds 1.5% by weight, creep strength is deteriorated. When Mn is added from the coating agent, Fe-Mn, metallic Mn, or the like can be added.
【００１６】Ｎｉ：０．４乃至１．５重量％
ＮｉはＭｎと同様に靭性を得るために不可欠な成分であ
る。０．４重量％未満ではその効果は発揮されず、１．
５重量％を超えるとクリープ強度を劣化させる。なお、
Ｎｉは被覆剤から添加する場合、金属Ｎｉ、Ｎｉ−Ｍｇ
等で添加することができる。 Ni: 0.4 to 1.5% by weight Ni is an essential component for obtaining toughness, like Mn. If it is less than 0.4% by weight, the effect is not exhibited.
If it exceeds 5% by weight, the creep strength is deteriorated. In addition,
Ni is metallic Ni or Ni-Mg when added from a coating agent.
Etc. can be added.
【００１７】Ｃｒ：６．０乃至１２．０重量％
Ｃｒは溶接金属の耐酸化性及び耐食性を向上させると共
に、固溶強化によるクリープ強度を維持する効果を有す
る。６．０重量％未満ではその効果が発揮されず、１
２．０重量％を超えるとδフェライトの析出により靭性
を劣化させる。なお、Ｃｒは被覆剤から添加する場合、
Ｆｅ−Ｃｒ、金属Ｃｒ等として添加することができる。 Cr: 6.0 to 12.0 wt% Cr has the effects of improving the oxidation resistance and corrosion resistance of the weld metal and maintaining the creep strength by solid solution strengthening. If it is less than 6.0% by weight, the effect is not exhibited and 1
If it exceeds 2.0% by weight, the toughness deteriorates due to the precipitation of δ ferrite. When Cr is added from the coating agent,
It can be added as Fe-Cr, metallic Cr, or the like.
【００１８】Ｍｏ：０．０５乃至０．２５重量％
ＭｏはＣｒと同様に、固溶強化及びクリープ温度で粒界
に析出するラーベス相を強化し、クリープ強度を維持す
る効果を有する。Ｍｏが０．０５重量％未満ではその効
果が発揮されず、０．２５重量％を超えると強度の上昇
により靭性を劣化させる。なお、Ｍｏは被覆剤から添加
する場合、Ｆｅ−Ｍｏ合金等として添加することができ
る。 Mo: 0.05 to 0.25 wt% Mo, like Cr, has the effects of solid solution strengthening and strengthening the Laves phase that precipitates at the grain boundaries at the creep temperature and maintains the creep strength. If Mo is less than 0.05% by weight, the effect is not exhibited, and if it exceeds 0.25% by weight, the strength is increased and the toughness is deteriorated. In addition, when adding Mo from a coating agent, it can be added as a Fe-Mo alloy etc.
【００１９】Ｔｉ：０．０１乃至０．０５重量％
Ｔｉは脱酸剤としてアークを安定させると共に、前述の
図１に示すように、Ｎ主体の炭窒化物であるＭＸを安定
化し、微細化させて、クリープ強度を著しく改善する。
Ｔｉが０．０１重量％未満ではその効果が発揮されず、
０．０５重量％を超えると強度の上昇と共に、靭性劣化
を引き起こす。なお、Ｔｉは被覆剤から添加する場合、
Ｆｅ−Ｔｉ等で添加することができる。 Ti: 0.01 to 0.05% by Weight Ti stabilizes the arc as a deoxidizer and stabilizes MX, which is a carbonitride containing N as a main component, as shown in FIG. To significantly improve the creep strength.
When Ti is less than 0.01% by weight, the effect is not exhibited,
If it exceeds 0.05% by weight, the strength is increased and the toughness is deteriorated. If Ti is added from the coating agent,
Fe-Ti or the like can be added.
【００２０】Ｖ：０．１０乃至０．４０重量％
Ｖは炭窒化物ＭＸの成分の一つとして析出し、ＭＸの安
定化に寄与し、クリープ強度を維持する効果を有する。
Ｖが０．１０重量％未満ではその効果が発揮されず、
０．４０重量％を超えると靭性を劣化させる。なお、Ｖ
は被覆剤から添加する場合には、Ｆｅ−Ｖ合金等として
添加することができる。 V: 0.10 to 0.40 wt% V precipitates as one of the components of the carbonitride MX, contributes to the stabilization of MX, and has the effect of maintaining the creep strength.
If V is less than 0.10% by weight, the effect is not exhibited,
If it exceeds 0.40% by weight, the toughness deteriorates. In addition, V
When added from a coating agent, it can be added as an Fe-V alloy or the like.
【００２１】Ｎｂ：０．０２乃至０．１０重量％
ＮｂはＴｉと同様に炭窒化物ＭＸを安定化し、微細化さ
せて、クリープ強度を著しく改善する。Ｎｂ含有量が
０．０２重量％未満ではその効果が発揮されず、０．１
０重量％を超えると強度の上昇と共に、靭性劣化を引き
起こす。なお、Ｎｂは被覆剤から添加する場合、Ｆｅ−
Ｎｂ合金等で添加することができる。 Nb: 0.02 to 0.10 wt% Nb stabilizes the carbonitride MX in the same manner as Ti, makes it finer, and significantly improves the creep strength. If the Nb content is less than 0.02% by weight, the effect is not exhibited and
If it exceeds 0% by weight, strength is increased and toughness is deteriorated. When Nb is added from the coating agent, Fe-
It can be added with Nb alloy or the like.
【００２２】Ｗ：０．７乃至２．０重量％
ＷはＭｏと同様に、固溶強化及びクリープ温度で粒界に
析出するラーベス相を強化し、クリープ強度を維持する
効果を有する。Ｗが０．７重量％未満ではその効果が発
揮されず、２．０重量％を超えると強度の上昇とδフェ
ライトの析出により靭性を劣化させる。なお、Ｗは被覆
剤から添加する場合は、Ｆｅ−Ｗ合金等として添加する
ことができる。 W: 0.7 to 2.0% by Weight W, like Mo, has the effects of solid solution strengthening and strengthening the Laves phase that precipitates at grain boundaries at the creep temperature and maintains the creep strength. If W is less than 0.7% by weight, the effect is not exhibited, and if it exceeds 2.0% by weight, the strength is increased and the precipitation of δ ferrite deteriorates the toughness. When W is added from the coating agent, it can be added as an Fe-W alloy or the like.
【００２３】Ｃｏ：０．１乃至２．０重量％以下
Ｃｏは、固溶強化によるクリープ強度の維持とδフェラ
イトを抑制する効果を有する。この効果を発揮するため
には、Ｃｏを０．１重量％以上添加する。但し、クリー
プ強度の効果は他の元素より小さいため、δフェライト
が析出しにくい成分系であれば、特に添加する必要はな
い。一方、過剰添加の場合は、強度上昇による靭性低下
が生じる。このため、Ｃｏ含有量は２．０重量％以下に
する必要がある。なお、Ｃｏは被覆剤から添加する場
合、金属Ｃｏ等として添加することができる。 Co: 0.1 to 2.0 wt% or less Co has an effect of maintaining creep strength by solid solution strengthening and suppressing δ ferrite. In order to exert this effect, 0.1% by weight or more of Co is added. However, since the effect of creep strength is smaller than that of other elements, if it is a component system in which δ ferrite is hard to precipitate, it is not particularly necessary to add it. On the other hand, in the case of excessive addition, the toughness decreases due to the increase in strength. Therefore, the Co content needs to be 2.0% by weight or less. When Co is added from the coating agent, it can be added as metallic Co or the like.
【００２４】Ｎ：０．０２乃至０．１０重量％
ＮはＭＸの主成分として、クリープ強度を維持する効果
を有する。Ｎが０．０２重量％未満ではその効果が発揮
されず、０．１０重量％を超えると靭性を劣化させる。
なお、Ｎは被覆剤から添加する場合は、窒化Ｃｒ等とし
て添加することができる。 N: 0.02 to 0.10 wt% N, as a main component of MX, has an effect of maintaining creep strength. If N is less than 0.02% by weight, the effect is not exhibited, and if it exceeds 0.10% by weight, toughness is deteriorated.
When N is added from the coating agent, it can be added as Cr nitride or the like.
【００２５】なお、この他の成分として被覆剤中には、
炭酸塩、弗化物、ＳｉＯ2、Ｍｇ等のアーク安定剤及び
スラグ生成剤と、Ｎａ2Ｏ、Ｋ2Ｏ、Ｌｉ2Ｏ等の粘結剤
が含まれる。また、Ｐ及びＳ等の不可避的不純物成分は
可及的に抑えることが望ましい。The other components in the coating agent are:
Arc stabilizers and slag forming agents such as carbonates, fluorides, SiO 2 and Mg, and binders such as Na 2 O, K 2 O and Li 2 O are included. Further, it is desirable to suppress unavoidable impurity components such as P and S as much as possible.
【００２６】[0026]
【実施例】以下、本発明の実施例について本発明の範囲
から外れる比較例と比較して説明する。下記表１に示す
化学成分の合金心線（直径４．０ｍｍ、長さ４００ｍ
ｍ）の外周に、被覆剤を塗布し、下記表２（本発明実施
例）、表３及び４（比較例）の成分を有する低水素系被
覆アーク溶接棒を作製した。なお、表２乃至４は、被覆
アーク溶接棒全体の組成であり、その重量％は被覆アー
ク溶接棒の全重量あたりの％である。更に、表２乃至４
に記載した成分以外に、その他の成分として、Ｆｅ、Ｍ
ｇ、Ｎａ2Ｏ、Ｋ2Ｏ、ＦｅＯ、Ｌｉ2Ｏ等が含まれてい
る。EXAMPLES Examples of the present invention will be described below in comparison with comparative examples that depart from the scope of the present invention. Alloy cores of chemical composition shown in Table 1 below (diameter 4.0 mm, length 400 m
A coating agent was applied to the outer periphery of m) to prepare a low hydrogen-based coated arc welding rod having the components shown in Table 2 (Examples of the present invention), Tables 3 and 4 (Comparative Example) below. It should be noted that Tables 2 to 4 show the composition of the entire coated arc welding rod, and the weight% thereof is% of the total weight of the coated arc welding rod. Further, Tables 2 to 4
In addition to the components described in, other components such as Fe and M
g, Na 2 O, K 2 O, FeO, Li 2 O, etc. are contained.
【００２７】そして、これらの溶接棒を使用して溶接試
験を実施した。ＡＳＴＭ Ａ２１３−Ｔ９１鋼板（板厚
２０ｍｍ、Ｖ開先）を、溶接入熱：１８乃至２２ｋＪ／
ｃｍ（溶接電圧１７０Ａ、溶接電流２３Ｖ、溶接速度約
１２ｃｍ／分）、溶接姿勢：下向、予熱及びパス間温
度：２００乃至２５０℃で行った。Then, a welding test was carried out using these welding rods. Weld heat input: ASTM A213-T91 steel plate (plate thickness 20 mm, V groove): 18 to 22 kJ /
cm (welding voltage 170 A, welding current 23 V, welding speed about 12 cm / min), welding posture: downward, preheating and interpass temperature: 200 to 250 ° C.
【００２８】その後、この試験板を７４０℃に８時間加
熱する熱処理（昇温・冷却：≦５０℃／ｈ）を行い、シ
ャルピー衝撃試験片（ＪＩＳ Ｚ３１１１ ４号）、ク
リープ試験片（ＪＩＳ Ｚ２２７２）を採取し、各規格
に準じて試験に供した。その結果を下記表５乃至７に示
す。なお、両試験共、試験片を各３本ずつ採取し、その
供試した試験片の平均値で特性を示した。シャルピー衝
撃試験は０℃、クリープ試験は６５０℃×１２５Ｎ／ｍ
ｍ2の条件で行った。溶接作業性の判定は、この溶接時
に官能評価（○：優、△：やや劣、×：劣）した。Thereafter, this test plate is heat-treated (heating / cooling: ≤50 ° C./h) by heating it to 740 ° C. for 8 hours, and a Charpy impact test piece (JIS Z3114) and a creep test piece (JIS Z2272). Was collected and subjected to the test according to each standard. The results are shown in Tables 5 to 7 below. In each test, three test pieces were sampled, and the average value of the test pieces tested showed the characteristics. Charpy impact test is 0 ℃, creep test is 650 ℃ × 125N / m
It was carried out under the condition of m 2 . The welding workability was evaluated by sensory evaluation (○: excellent, Δ: slightly inferior, ×: inferior) during this welding.
【００２９】[0029]
【表１】 [Table 1]
【００３０】[0030]
【表２】 [Table 2]
【００３１】[0031]
【表３】 [Table 3]
【００３２】[0032]
【表４】 [Table 4]
【００３３】[0033]
【表５】 [Table 5]
【００３４】[0034]
【表６】 [Table 6]
【００３５】[0035]
【表７】 [Table 7]
【００３６】表５に示すように、供試棒Ｎｏ．１乃至Ｎ
ｏ．６は本発明の実施例であり、いずれも靭性、クリー
プ強度及び溶接作業性が良好であった。一方、比較例
（Ｎｏ．Ｎ１乃至Ｎｏ．Ｎ２３）は、これらの性能が低
いものであった。As shown in Table 5, the test bar No. 1 to N
o. No. 6 is an example of the present invention, and all had good toughness, creep strength and welding workability. On the other hand, the comparative examples (No. N1 to No. N23) had low performance.
【００３７】即ち、ＮＯ．Ｎ１はＣが０．０３重量％と
少ないため、クリープ破断時間が短く、Ｎｏ．Ｎ２は
０．１１重量％と多すぎるため、靭性が劣化した。Ｎ
ｏ．Ｎ３はＳｉが０．４５重量％と少ないため、溶接作
業性が劣化し、Ｎｏ．Ｎ４は２．０３重量％と多すぎる
ために、靭性が劣化した。Ｎｏ．Ｎ５はＭｎが０．４６
重量％と少ないために、靭性が劣化し、Ｎｏ．Ｎ６は
１．５４重量％と多すぎるために、クリープ強度が劣化
した。Ｎｏ．Ｎ７はＮｉが０．３８重量％と少ないた
め、靭性が劣化し、Ｎｏ．Ｎ８は１．５５重量％と多す
ぎるために、クリープ強度が劣化した。Ｎｏ．Ｎ９はＣ
ｒが５．９３重量％少ないために、クリープ強度が劣化
し、Ｎｏ．Ｎ１０は１２．０８重量％と多すぎるため
に、靭性が劣化した。Ｎｏ．Ｎ１１はＭｏが０．０３重
量％と少ないために、クリープ強度が劣化し、Ｎｏ．Ｎ
１２は０．２８重量％と多すぎるために、靭性が劣化し
た。Ｎｏ．Ｎ１３はＴｉが０．００７重量％と少ないた
めに、クリープ強度が劣化し、Ｎｏ．Ｎ１４は０．０５
４重量％と多すぎるために、靭性が劣化した。Ｎｏ．Ｎ
１５はＶが０．０８重量％と少ないために、クリープ強
度が劣化し、Ｎｏ．Ｎ１６は０．４３重量％と多すぎる
ために、靭性が劣化した。Ｎｏ．Ｎ１７はＮｂが０．０
１７重量％と少ないために、クリープ強度が劣化し、Ｎ
ｏ．Ｎ１８は０．１１重量％と多すぎるために、靭性が
劣化した。Ｎｏ．Ｎ１９はＷが０．６６重量％と少ない
ために、クリープ強度が劣化し、Ｎｏ．Ｎ２０は２．０
４重量％と多すぎる、靭性が劣化した。ＮＯ．Ｎ２１は
Ｃｏが２．０５重量％と多すぎるために、靭性が劣化し
た。Ｎｏ．Ｎ２２はＮが０．０１８重量％と少ないため
に、クリープ強度が劣化し、ＮＯ．Ｎ２３は０．１１重
量％と多すぎるために、靭性が劣化した。That is, NO. Since the C content of N1 is as small as 0.03% by weight, the creep rupture time is short, and Since N2 was 0.11% by weight, which was too large, the toughness deteriorated. N
o. Since N3 has a low Si content of 0.45% by weight, welding workability deteriorates. Since N4 was 2.03% by weight, which was too large, the toughness deteriorated. No. Mn of N5 is 0.46
Since it is as small as wt%, the toughness deteriorates, and No. Since N6 was 1.54% by weight, which was too large, the creep strength was deteriorated. No. Since N7 has a small Ni content of 0.38% by weight, its toughness deteriorates. Since N8 was 1.55% by weight, which was too large, the creep strength deteriorated. No. N9 is C
Since the r is less by 5.93% by weight, the creep strength is deteriorated and No. Since N10 was too much as 12.08% by weight, the toughness deteriorated. No. Since N11 has a small Mo content of 0.03% by weight, its creep strength deteriorates. N
No. 12 was 0.28% by weight, which was too much, so that the toughness deteriorated. No. Since N13 has a small Ti content of 0.007% by weight, its creep strength deteriorates. N14 is 0.05
The toughness was deteriorated because the amount was too much as 4% by weight. No. N
No. 15 had a V content as low as 0.08% by weight, so the creep strength deteriorated. Since N16 was 0.43% by weight, which was too much, the toughness deteriorated. No. N17 has Nb of 0.0
Since it is as small as 17% by weight, the creep strength deteriorates and N
o. Since N18 was too much as 0.11% by weight, the toughness deteriorated. No. Since N19 has a small W of 0.66% by weight, the creep strength is deteriorated, and No. N20 is 2.0
4% by weight, which is too much, and the toughness deteriorated. NO. Since N21 is too much as 2.05% by weight, the toughness is deteriorated. No. Since N22 is as small as 0.018% by weight, the creep strength is deteriorated, and NO. Since N23 was too much as 0.11% by weight, the toughness deteriorated.
【００３８】[0038]
【発明の効果】以上述べたように、本発明によれば、低
水素系被覆アーク溶接棒において心線及び被覆剤の全体
の組成を規定することにより、高Ｃｒフェライト系耐熱
鋼を溶接した場合に、極めて優れた靭性及びクリープ性
能の溶接金属を得ることができ、溶接作業性も優れてい
る。従って、本発明の高Ｃｒフェライト系耐熱鋼用低水
素系被覆ア−ク溶接棒は、各種発電ボイラ及び化学圧力
容器の安全性と耐久性の向上に寄与する効果は顕著であ
る。As described above, according to the present invention, when the high Cr ferritic heat resistant steel is welded by defining the overall composition of the core wire and the coating material in the low hydrogen coated arc welding rod. In addition, a weld metal having extremely excellent toughness and creep performance can be obtained, and welding workability is also excellent. Therefore, the low-hydrogen coated arc welding rod for high Cr ferritic heat-resistant steel of the present invention has a remarkable effect of contributing to the improvement of safety and durability of various power generation boilers and chemical pressure vessels.
【図１】被覆アーク溶接棒のＴｉ量と靭性及びクリープ
強度の関係を示す図である。FIG. 1 is a diagram showing the relationship between the Ti content of a coated arc welding rod and its toughness and creep strength.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 畠 英雄 兵庫県神戸市西区高塚台１丁目５番５号 株式会社神戸製鋼所神戸総合技術研究 所内 (72)発明者 畑野 等 兵庫県神戸市西区高塚台１丁目５番５号 株式会社神戸製鋼所神戸総合技術研究 所内 (72)発明者 佐藤 統宣 神奈川県藤沢市宮前字裏河内100番１ 株式会社神戸製鋼所藤沢事業所内 (56)参考文献 特開 平７−155988（ＪＰ，Ａ) 特開 平９−122972（ＪＰ，Ａ) 特開 平４−305396（ＪＰ，Ａ) 特開 平１−215491（ＪＰ，Ａ) 特開 平９−267190（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) B23K 35/30 B23K 35/365 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Hideo Hatake, 1-5-5 Takatsukadai, Nishi-ku, Kobe-shi, Hyogo Prefecture Kobe Steel Co., Ltd. Kobe Research Institute (72) Inventor Hatano, etc. Takatsuka, Nishi-ku, Kobe-shi, Hyogo Prefecture No. 1-5-5 Kobe Steel Co., Ltd., Kobe Research Institute (72) Inventor Toshinori Sato 100-1 Urakawachi, Miyamae, Fujisawa-shi, Kanagawa Kobe Steel Co., Ltd., Fujisawa Works (56) References Special Kaihei 7-155988 (JP, A) JP 9-122972 (JP, A) JP 4-305396 (JP, A) JP 1-215491 (JP, A) JP 9-267190 ( JP, A) (58) Fields investigated (Int.Cl. 7 , DB name) B23K 35/30 B23K 35/365
Claims (2)
被覆アーク溶接棒全重量当たり、Ｃ：０．０４乃至０．
１０重量％、Ｓｉ：０．５乃至２．０重量％、Ｍｎ：
０．５乃至１．５重量％、Ｎｉ：０．４乃至１．５重量
％、Ｃｒ：６．０乃至１２．０重量％、Ｍｏ：０．０５
乃至０．２５重量％、Ｔｉ：０．０１乃至０．０５重量
％、Ｖ：０．１０乃至０．４０重量％、Ｎｂ：０．０２
乃至０．１０重量％、Ｗ：０．７乃至２．０重量％、
Ｎ：０．０２乃至０．１０重量％を含有したことを特徴
とする高Ｃｒフェライト系耐熱鋼用低水素系被覆アーク
溶接棒。1. In one or both of the core wire and the coating,
Based on the total weight of the coated arc welding rod, C: 0.04 to 0.
10% by weight, Si: 0.5 to 2.0% by weight, Mn:
0.5 to 1.5% by weight, Ni: 0.4 to 1.5% by weight, Cr: 6.0 to 12.0% by weight, Mo: 0.05
To 0.25 wt%, Ti: 0.01 to 0.05 wt%, V: 0.10 to 0.40 wt%, Nb: 0.02
To 0.10% by weight, W: 0.7 to 2.0% by weight,
N: 0.02 to 0.10% by weight, a low hydrogen coated arc welding rod for high Cr ferritic heat resistant steel, characterized in that
被覆アーク溶接棒全重量当たり、Ｃ：０．０４乃至０．
１０重量％、Ｓｉ：０．５乃至２．０重量％、Ｍｎ：
０．５乃至１．５重量％、Ｎｉ：０．４乃至１．５重量
％、Ｃｒ：６．０乃至１２．０重量％、Ｍｏ：０．０５
乃至０．２５重量％、Ｔｉ：０．０１乃至０．０５重量
％、Ｖ：０．１０乃至０．４０重量％、Ｎｂ：０．０２
乃至０．１０重量％、Ｗ：０．７乃至２．０重量％、Ｃ
ｏ：０．１乃至２．０重量％、Ｎ：０．０２乃至０．１
０重量％を含有したことを特徴とする高Ｃｒフェライト
系耐熱鋼用低水素系被覆アーク溶接棒。2. In one or both of the core wire and the coating,
Based on the total weight of the coated arc welding rod, C: 0.04 to 0.
10% by weight, Si: 0.5 to 2.0% by weight, Mn:
0.5 to 1.5% by weight, Ni: 0.4 to 1.5% by weight, Cr: 6.0 to 12.0% by weight, Mo: 0.05
To 0.25 wt%, Ti: 0.01 to 0.05 wt%, V: 0.10 to 0.40 wt%, Nb: 0.02
To 0.10% by weight, W: 0.7 to 2.0% by weight, C
o: 0.1 to 2.0% by weight, N: 0.02 to 0.1
A low hydrogen coated arc welding rod for high Cr ferritic heat resistant steel, characterized by containing 0% by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP33620097A JP3375868B2 (en) | 1997-12-05 | 1997-12-05 | Low hydrogen coated arc welding rod for high Cr ferritic heat resistant steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP33620097A JP3375868B2 (en) | 1997-12-05 | 1997-12-05 | Low hydrogen coated arc welding rod for high Cr ferritic heat resistant steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11170087A JPH11170087A (en) | 1999-06-29 |
| JP3375868B2 true JP3375868B2 (en) | 2003-02-10 |
Family
ID=18296680
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP33620097A Expired - Lifetime JP3375868B2 (en) | 1997-12-05 | 1997-12-05 | Low hydrogen coated arc welding rod for high Cr ferritic heat resistant steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3375868B2 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6641084B2 (en) * | 2014-12-25 | 2020-02-05 | 株式会社神戸製鋼所 | Low hydrogen coated arc welding rod with excellent resistance to bar burn during welding |
| JP6829090B2 (en) | 2017-01-31 | 2021-02-10 | 株式会社神戸製鋼所 | Shielded metal arc welding rod |
| JP6914182B2 (en) * | 2017-12-25 | 2021-08-04 | 株式会社神戸製鋼所 | Shielded metal arc welding rod |
| JP6688344B2 (en) * | 2018-07-12 | 2020-04-28 | 株式会社神戸製鋼所 | Low-hydrogen coated arc welding rod |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2607594B2 (en) * | 1988-02-24 | 1997-05-07 | 日本鋼管株式会社 | Coated arc welding rod for Cr-Mo low alloy steel |
| JPH0825060B2 (en) * | 1991-03-29 | 1996-03-13 | 新日本製鐵株式会社 | Low-hydrogen coated arc welding rod |
| JP3217567B2 (en) * | 1993-12-03 | 2001-10-09 | 新日本製鐵株式会社 | Covered arc welding rod for high Cr ferritic heat resistant steel |
| JPH09122972A (en) * | 1995-10-30 | 1997-05-13 | Nippon Steel Corp | Coated electrode for high-cr ferrite heat resisting steel |
| JP3375817B2 (en) * | 1996-03-29 | 2003-02-10 | 株式会社神戸製鋼所 | Welding wire for high chromium ferritic steel |
-
1997
- 1997-12-05 JP JP33620097A patent/JP3375868B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH11170087A (en) | 1999-06-29 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP6852809B2 (en) | Austenitic heat-resistant steel Welded metal, welded joints, welding materials for austenitic heat-resistant steel, and methods for manufacturing welded joints | |
| JPS59176501A (en) | Boiler tube | |
| WO2014119189A1 (en) | Coated electrode | |
| JPH10280085A (en) | Welding material for low cr ferritic steel, excellent in toughness | |
| JP3329261B2 (en) | Welding materials and welded joints for high temperature high strength steel | |
| JP2017047472A (en) | Wire for submerged arc welding | |
| KR102658542B1 (en) | Covered arc welding rod for high Cr ferritic heat-resistant steel | |
| JP3375868B2 (en) | Low hydrogen coated arc welding rod for high Cr ferritic heat resistant steel | |
| JP2000234140A (en) | Steel for boiler excellent in electric resistance weldability and electric resistance welded boiler steel tube using it | |
| WO2017154754A1 (en) | Welded metal and welded structure containing said welded metal | |
| WO1994026947A1 (en) | High-strength austenitic heat-resisting steel with excellent weldability and good high-temperature corrosion resistance | |
| JP4377869B2 (en) | Boiler steel excellent in ERW weldability and ERW boiler steel pipe using the same | |
| JP3552517B2 (en) | Method for welding high Cr ferritic heat resistant steel and method for manufacturing welded steel pipe | |
| JPS5914097B2 (en) | Ferritic heat-resistant steel with improved toughness | |
| JP3582463B2 (en) | Welding material and metal for low alloy heat resistant steel | |
| JP3527640B2 (en) | Weld metal for high Cr ferritic heat resistant steel | |
| JP3388998B2 (en) | High strength austenitic heat-resistant steel with excellent weldability | |
| JP7295418B2 (en) | welding material | |
| JPH07204885A (en) | Ferrite steel welding material having excellent high-temperature weld crack resistance | |
| JP2594265B2 (en) | TIG welding wire for 9Cr-Mo steel | |
| JP3194207B2 (en) | Covered arc welding rod for high Cr ferritic heat resistant steel | |
| JPS63183155A (en) | High-strength austenitic heat-resisting alloy | |
| JP3367831B2 (en) | Welding material for high strength ferritic heat resistant steel | |
| JPH06262388A (en) | Coated electrode for heat-resisting steel of high cr ferrite | |
| JP3367824B2 (en) | Welding material for heat resistant ferritic steel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20081129 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20081129 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20091129 Year of fee payment: 7 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20091129 Year of fee payment: 7 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20101129 Year of fee payment: 8 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20111129 Year of fee payment: 9 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20121129 Year of fee payment: 10 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20131129 Year of fee payment: 11 |
|
| EXPY | Cancellation because of completion of term |